EP2439291A1 - Acier à plusieurs phases, produit plat laminé à froid fabriqué à partir d'un tel acier à plusieurs phases et son procédé de fabrication - Google Patents

Acier à plusieurs phases, produit plat laminé à froid fabriqué à partir d'un tel acier à plusieurs phases et son procédé de fabrication Download PDF

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Publication number
EP2439291A1
EP2439291A1 EP10186555A EP10186555A EP2439291A1 EP 2439291 A1 EP2439291 A1 EP 2439291A1 EP 10186555 A EP10186555 A EP 10186555A EP 10186555 A EP10186555 A EP 10186555A EP 2439291 A1 EP2439291 A1 EP 2439291A1
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EP
European Patent Office
Prior art keywords
cold
temperature
annealing
steel
multiphase steel
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Application number
EP10186555A
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German (de)
English (en)
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EP2439291B1 (fr
Inventor
Ekaterina Dr. Bocharova
Dorothea Dr. Mattissen
Roland Dr. Sebald
Daniel Dr. Krizan
Andreas Dr. Pichler
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Voestalpine Stahl GmbH
ThyssenKrupp Steel Europe AG
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Voestalpine Stahl GmbH
ThyssenKrupp Steel Europe AG
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
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Application filed by Voestalpine Stahl GmbH, ThyssenKrupp Steel Europe AG filed Critical Voestalpine Stahl GmbH
Priority to EP10186555.8A priority Critical patent/EP2439291B1/fr
Priority to KR1020137011653A priority patent/KR101850122B1/ko
Priority to US13/877,816 priority patent/US20130248055A1/en
Priority to CN201180048743.0A priority patent/CN103237905B/zh
Priority to PCT/EP2011/066774 priority patent/WO2012045613A1/fr
Priority to JP2013532120A priority patent/JP6093702B2/ja
Publication of EP2439291A1 publication Critical patent/EP2439291A1/fr
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a method for producing a cold-rolled product, a multiphase steel and a cold rolled flat product produced from such a multiphase steel by cold rolling.
  • the "flat products” according to the invention may be sheets, strips, blanks obtained therefrom or comparable products. If this is referred to as "cold flat products", it means flat products produced by cold rolling.
  • a multiphase steel which should have a balanced property profile in this respect, is from the EP 1 367 143 A1 known.
  • EP 1 367 143 A1 known.
  • the known steel should also have a particularly good weldability.
  • the known steel contains to 0.03 - 0.25 wt .-% C, by its presence in combination with the other alloying elements tensile strengths of at least 700 MPa to be achieved.
  • the strength of the known steel is to be supported by Mn in contents of 1.4-3.5% by weight.
  • Al is used in the melting of the known steel as an oxidizing agent and may be present in the steel in amounts of up to 0.1% by weight.
  • the known steel may also have up to 0.7% by weight of Si, the presence of which stabilizes the ferritic-martensitic structure of the steel.
  • Cr is added to the known steel in amounts of 0.05-1% by weight in order to reduce the influence of the heat introduced by the welding process in the region of the weld.
  • Nb should additionally have a positive influence on the deformability of the steel, since its presence brings about a thinning of the ferrite grain.
  • 0.05 to 1% by weight of Mo, 0.02 to 0.5% by weight of V, 0.005 to 0.05% by weight of Ti and 0.0002 to 0.002% by weight of the known steel can be used.
  • % B are added. Mo and V contribute to the hardenability of the known steel, while Ti and B should additionally have a positive effect on the strength of the steel.
  • Another, also made of a high strength multiphase steel, well malleable steel sheet is from the EP 1 589 126 B1 known.
  • This known steel sheet contains 0.10-0.28 wt% C, 1.0-2.0 wt% Si, 1.0-3.0 wt% Mn, 0.03-0.10 Wt% Nb, up to 0.5 wt% A1, up to 0.15 wt% P, up to 0.02 wt% S.
  • the steel sheet up to 1.0 wt% Mo, up to 0.5 wt% Ni, up to 0.5 wt% Cu, to 0.003 wt% Ca, up to 0.003 wt .-% rare earth metals, up to 0.1 wt .-% Ti or up to 0.1 wt .-% V be present.
  • the structure of the known steel sheet based on its overall structure, has a retained austenite content of 5 to 20% and at least 50% bainitic ferrite. At the same time, the proportion of polygonal ferrite in the structure of the known steel sheet should be at most 30%.
  • the object of the invention was to provide a method for producing a cold-flat product from a multiphase steel with TRIP properties, which has a further increased strength with simultaneously high elongation at break. Similarly, a multi-phase steel and a flat product should be created with this combination of properties.
  • the solution of the above-mentioned object consists of a cold flat product designed according to claim 16.
  • a multiphase steel according to the invention contains (in% by weight) C: 0.14-0.25%, Mn: 1.7-2.5%, Si: 1.4-2.0%, A1: ⁇ 0.1 1%, Cr: ⁇ 0.1 1%, Mo: ⁇ 0.05%, Nb: 0.02-0.06%, S: up to 0.01%, P: up to 0.02%, N: up to 0.01%, and optionally at least one element from the group "Ti, B, V" according to the following proviso: Ti: up to 0.1%, B: up to 0.002%, V : up to 0.15%, balance iron and unavoidable impurities.
  • the steel according to the invention is melted and cast into a preliminary product.
  • This precursor may be a slab or a thin slab.
  • the precursor is then reheated to a temperature of 1100-1300 ° C, if necessary, to obtain a uniformly warmed microstructure of the starting product.
  • Reheating temperatures of max. 1250 ° C, in particular max. 1220 ° C lead at optimized production costs to an improved surface of the product according to the invention.
  • the precursor is then hot rolled to a hot strip.
  • the final temperature of the hot rolling is 820-950 ° C., in order to ensure a good microstructure exit situation for the cooling on the outfeed roller table which has passed through after the hot rolling.
  • the hot strip obtained is then wound into a coil at a coiler temperature of 400-750 ° C., in particular 530-600 ° C., in order to obtain the later Cold rolling carried out without being able to carry out large rolling forces and to avoid grain boundary oxidation.
  • the hot strip After coiling, the hot strip at cold rolling degrees of 30-80%, especially 50-70%, cold-rolled to a cold flat product to ensure a sufficiently high driving force for the recrystallization processes in the subsequent annealing.
  • the resulting cold-rolled product is then subjected to a heat treatment comprising a continuous annealing and overaging of the cold-rolled product.
  • the annealing temperature set in the continuous annealing is according to the invention at least 20 ° C higher than the A c1 temperature of the steel and must not exceed the A c3 temperature of the steel.
  • the overaging temperature set in the overaging treatment is typically 350-500 ° C, especially 370-460 ° C, to cause further carbonization of the austenite.
  • the continuous annealing prescribed by the invention with an annealing temperature extending to at most the A c3 temperature causes the microstructure of the cold-rolled product produced according to the invention to have comparatively high martensite contents of 12-40% by volume and, consequently, a high level of tensile strength R m of at least 980 Reached MPa.
  • the steel produced according to the invention has a good formability, which manifests itself in a transverse elongation A 80 of at least 15%.
  • the yield strength R eL of the steel according to the invention is regularly above 500 MPa.
  • the multiphase steel according to the invention has TRIP properties.
  • the annealing time over which the cold flat product is annealed at the annealing temperature is typically at most 300 seconds to allow a sufficiently high level of carbon-enriched austenite to form in the two-phase region of the steel.
  • the duration of the over-aging treatment after annealing can be up to 800 s to optimally stabilize retained austenite.
  • the cold-rolled product can be accelerated after annealing from the annealing temperature corresponding to the maximum of the A c3 temperature at a cooling rate of at least 5 ° C / s to a 500 ° C Intermediate temperature to be cooled.
  • the annealing of the cold flat product can be carried out in the course of a fire coating, in which the cold flat product is provided with a metallic protective coating.
  • the cold strip produced according to the invention with a protective layer after the heat treatment by electrolytic coating or another deposition method.
  • the cold-rolled strip obtained may also be subjected to re-rolling at degrees of deformation of up to 3.0% in order to improve its dimensional stability, surface finish and mechanical properties.
  • the hot strip may be subjected to annealing prior to cold rolling. This can be advantageously carried out as Haubenglühung or continuous annealing.
  • the at the the cold rolling preparatory annealing set annealing temperatures are typically 400-700 ° C.
  • Carbon increases the amount and the stability of the retained austenite in a steel according to the invention. Therefore, in the steel of the present invention, at least 0.14 wt% of carbon is present to stabilize the austenite to room temperature and to prevent complete conversion of the austenite formed in an annealing treatment into martensite, ferrite or bainite, and bainitic ferrite, respectively.
  • at least 0.14 wt% of carbon is present to stabilize the austenite to room temperature and to prevent complete conversion of the austenite formed in an annealing treatment into martensite, ferrite or bainite, and bainitic ferrite, respectively.
  • over 0.25 wt .-% lying carbon contents have a negative effect on the weldability.
  • the positive effects of carbon in steel according to the invention can be used particularly reliably if C is present in amounts of 0.19-0.24% by weight, in particular up to 0.23% by weight, with a minimum content of 0.21 wt .-% C is particularly advantageous.
  • Mn Like C, Mn contributes to the strength and increase the amount and stability of the retained austenite. However, excessive Mn levels increase the risk of segregation. They also have a negative effect on the elongation at break, since the ferrite and bainite conversions are greatly delayed and, as a result, comparatively high amounts of martensite remain in the microstructure.
  • the Mn content of a steel according to the invention is set at 1.7-2.5% by weight.
  • Steel according to the invention contains 1.4-2.0% by weight of Si. At levels greater than 1.4% by weight, Si assists in stabilizing the retained austenite and suppresses it In the course of the processing of the steel according to the invention, over-aging treatment carried out the carbide formation in the bainite stage. The bainite transformation does not proceed completely due to the presence of Si, so that only bainitic ferrite is formed and carbide formation does not occur. In this way, the present invention desired stability of carbon-enriched retained austenite is achieved.
  • Si contributes to increasing strength by solid solution strengthening. At levels of more than 2% by weight, however, deterioration of the surface quality and the risk of embrittlement during hot rolling must be expected.
  • a steel according to the invention When producing a steel according to the invention, Al is used for deoxidation.
  • a steel according to the invention therefore has Al contents of less than 0.1% by weight.
  • the Cr content is limited to less than 0.1% by weight and the Mo content of a steel according to the invention is limited to less than 0.05% by weight.
  • a steel according to the invention contains Nb in amounts of 0.02-0.06% by weight and optionally one or more of the elements "Ti, V, B" in order to increase the strength of the steel according to the invention.
  • Nb, Ti and V form with the C and N present in the steel according to the invention very fine excretions. These precipitates increase strength and yield strength by particle hardening and grain refining. The grain refining is also of great advantage for the forming properties of the steel.
  • Ti still binds N during solidification or very high temperatures, so that possible negative effects of this element on the properties of the steel according to the invention are minimized.
  • up to 0.1% by weight of Ti and up to 0.15% by weight of V can be added to a steel according to the invention in addition to the Nb which is always present.
  • the positive influence of the presence of Ti with respect to the setting of the N contents can be used particularly purposefully if the Ti content "% Ti" of a multiphase steel according to the invention fulfills the following condition [3]: % Ti ⁇ 3 . 4 x % N . where "% N" denotes the respective N content of the multiphase steel.
  • the positive effect of Ti in a steel according to the invention occurs particularly reliably when its Ti content is at least 0.01% by weight.
  • the ferrite formation can be delayed upon cooling, so that a larger amount of austenite is present in the bainite. As a result, the amount and the stability of the retained austenite can be increased.
  • bainitic ferrite is formed instead of normal ferrite, which contributes to increasing the yield strength.
  • At least 10% by volume of ferrite, in particular at least 12% by volume of ferrite, and at least 6% by volume of retained austenite and optionally 5-40% by volume of bainite are present in the structure of a steel according to the invention in order to achieve the desired high strength and On the other hand, to ensure good deformability.
  • Up to 90% by volume of the microstructure of ferrite can be used, depending on the amount of the remaining microstructure constituents, and the residual austenite contents of the microstructure can amount to a maximum of 25% by volume.
  • Contents of at least 12 vol.% Martensite in the structure of the steel according to the invention contribute to its strength, wherein the martensite content to max. 40 Vol .-% should be limited in order to ensure sufficient extensibility of the steel according to the invention.
  • the retained austenite of a steel according to the invention is preferably enriched in carbon such that it is present in accordance with the method described in the article of A. Zarei Hanzaki et al. in ISIJ Int. Vol. 35, No 3, 1995, pp. 324 - 331 published formula [1] calculated C inRA content is more than 0.6 wt .-%.
  • C INRA a RA - a ⁇ / 0 . 0044 with a ⁇ : 0.3578 nm (lattice constant of austenite); a RA : respective lattice parameter of the retained austenite after final cooling in nm measured on the finished cold strip.
  • the amount of carbon present in the retained austenite substantially affects the TRIP properties and ductility of a steel according to the invention. Accordingly, it is advantageous if the C inRA content is as high as possible.
  • G RA % RA x C INRA with% RA: residual austenite content of the multiphase steel in% by volume; C inRA : C content of retained austenite calculated according to formula [1].
  • each of the cold-rolled products after the cold rolling has been subjected to a heat treatment, the annealing at an annealing temperature GT over an annealing time GZ, followed by accelerated cooling with a Cooling rate V to 500 ° C and an overaging treatment at an overaging temperature UAT over an overaging time UAt included.
  • the different heat treatment variants used are given in Table 2.
  • Table 3 also shows for each of the cold-rolled products K1-K23 the tensile strength R m , the yield strength R eL , the transverse elongation A 80 in the transverse direction, the residual austenite content RA, the C content C inRA of the retained austenite, the quality G RA of the retained austenite and the martensite content M.
  • Table 1 (content by weight in%, balance iron and unavoidable impurities) melt C Si Mn al Nb V Ti P S N B A c3 A c1 S1 0.217 1.75 1,85 0,021 0.04 0.01 0.01 0,004 0,003 0.0016 0.0004 853 754 S2 0.24 1.75 1.8 0, 021 0.04 0.01 0.02 0,004 0,003 0.0036 0.001 853 755 S3 0.217 1.75 2.2 0,021 0.04 0.01 0.01 0.01 0,004 0,003 0.0049 0.0004 842 750 S4 0.23 1.65 2.0 0.05 0.04 0.02 0.01 0,015 0,003 0.005 0.0005 861 750 S5 0.21 1.75 1,85 0.02 0.04 0.01 0.01 0,004 0,002 0.0016 0.0004 854 754 S6 0.226 1.44 2.47 0.08 0.06 0.02 0.01 0.005 0,002 0.0025 0.0003 844 738 S7 0.211 1.97 1.76 0.048 0.02

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)
EP10186555.8A 2010-10-05 2010-10-05 Acier à plusieurs phases, produit plat laminé à froid fabriqué à partir d'un tel acier à plusieurs phases et son procédé de fabrication Active EP2439291B1 (fr)

Priority Applications (6)

Application Number Priority Date Filing Date Title
EP10186555.8A EP2439291B1 (fr) 2010-10-05 2010-10-05 Acier à plusieurs phases, produit plat laminé à froid fabriqué à partir d'un tel acier à plusieurs phases et son procédé de fabrication
KR1020137011653A KR101850122B1 (ko) 2010-10-05 2011-09-27 복합조직강, 복합조직강으로 제조된 냉연 평판 제품 및 제조 방법
US13/877,816 US20130248055A1 (en) 2010-10-05 2011-09-27 Multi-Phase Steel, Cold-Rolled Flat Product Produced from Such a Multi-Phase Steel and Method for Producing It
CN201180048743.0A CN103237905B (zh) 2010-10-05 2011-09-27 多相钢，由该类多相钢制成的、冷轧的扁钢制品以及该制造方法
PCT/EP2011/066774 WO2012045613A1 (fr) 2010-10-05 2011-09-27 Acier multiphases, produit plat laminé à froid composé d'un tel acier multiphases et procédé de fabrication dudit produit plat
JP2013532120A JP6093702B2 (ja) 2010-10-05 2011-09-27 多相鋼から作られた冷間圧延平鋼製品およびその製造方法

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP10186555.8A EP2439291B1 (fr) 2010-10-05 2010-10-05 Acier à plusieurs phases, produit plat laminé à froid fabriqué à partir d'un tel acier à plusieurs phases et son procédé de fabrication

Publications (2)

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EP2439291A1 true EP2439291A1 (fr) 2012-04-11
EP2439291B1 EP2439291B1 (fr) 2013-11-27

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US (1) US20130248055A1 (fr)
EP (1) EP2439291B1 (fr)
JP (1) JP6093702B2 (fr)
KR (1) KR101850122B1 (fr)
CN (1) CN103237905B (fr)
WO (1) WO2012045613A1 (fr)

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WO2014019964A1 (fr) * 2012-07-30 2014-02-06 Tata Steel Nederland Technology Bv Procédé de production d'une bande d'acier à haute résistance présentant une bonne aptitude à l'emboutissage profond et acier à haute résistance ainsi produit
JP2015014026A (ja) * 2013-07-04 2015-01-22 新日鐵住金株式会社 冷延鋼板およびその製造方法
CN104404367A (zh) * 2014-12-10 2015-03-11 东北大学 一种高强度高塑性冷轧低碳钢及其制备方法
CN105247082A (zh) * 2013-04-01 2016-01-13 日立金属株式会社 刀具用钢的生产方法
CN108165709A (zh) * 2016-08-29 2018-06-15 武汉佰起科技有限公司 一种用于弹簧片的带钢加工工艺
EP3390040B1 (fr) 2015-12-15 2020-08-26 Tata Steel IJmuiden B.V. Bande d'acier galvanisé à chaud haute résistance
CN115181893A (zh) * 2021-04-02 2022-10-14 宝山钢铁股份有限公司 1180MPa级低碳低合金热镀锌TRIP钢及快速热处理热镀锌制造方法

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PL3276030T3 (pl) 2015-03-23 2020-09-21 Nippon Steel Corporation Blacha stalowa cienka walcowana na gorąco i sposób jej wytwarzania oraz sposób wytwarzania blachy stalowej cienkiej walcowanej na zimno
DE102017123236A1 (de) * 2017-10-06 2019-04-11 Salzgitter Flachstahl Gmbh Höchstfester Mehrphasenstahl und Verfahren zur Herstellung eines Stahlbandes aus diesem Mehrphasenstahl
EP3797176A1 (fr) * 2018-05-22 2021-03-31 ThyssenKrupp Steel Europe AG Pièce façonnée en tôle composée d'acier et présentant une résistance élevée à la traction, et procédé de fabrication de ladite pièce
CN111534739A (zh) * 2020-02-17 2020-08-14 本钢板材股份有限公司 一种980MPa级高成形性冷轧相变诱导塑性钢及其制备方法
CN115181892B (zh) * 2021-04-02 2023-07-11 宝山钢铁股份有限公司 1180MPa级别低碳低合金TRIP钢及快速热处理制造方法
KR102372546B1 (ko) * 2021-07-27 2022-03-10 현대제철 주식회사 연신율이 우수한 초고강도 강판 및 그 제조방법
DE102022102418A1 (de) 2022-02-02 2023-08-03 Salzgitter Flachstahl Gmbh Hochfestes schmelztauchbeschichtetes Stahlband mit durch Gefügeumwandlung bewirkter Plastizität und Verfahren zu dessen Herstellung

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WO2014019964A1 (fr) * 2012-07-30 2014-02-06 Tata Steel Nederland Technology Bv Procédé de production d'une bande d'acier à haute résistance présentant une bonne aptitude à l'emboutissage profond et acier à haute résistance ainsi produit
CN105247082A (zh) * 2013-04-01 2016-01-13 日立金属株式会社 刀具用钢的生产方法
JP2015014026A (ja) * 2013-07-04 2015-01-22 新日鐵住金株式会社 冷延鋼板およびその製造方法
CN104404367A (zh) * 2014-12-10 2015-03-11 东北大学 一种高强度高塑性冷轧低碳钢及其制备方法
EP3390040B1 (fr) 2015-12-15 2020-08-26 Tata Steel IJmuiden B.V. Bande d'acier galvanisé à chaud haute résistance
EP3390040B2 (fr) † 2015-12-15 2023-08-30 Tata Steel IJmuiden B.V. Bande d'acier galvanisé à chaud haute résistance
CN108165709A (zh) * 2016-08-29 2018-06-15 武汉佰起科技有限公司 一种用于弹簧片的带钢加工工艺
CN115181893A (zh) * 2021-04-02 2022-10-14 宝山钢铁股份有限公司 1180MPa级低碳低合金热镀锌TRIP钢及快速热处理热镀锌制造方法
CN115181893B (zh) * 2021-04-02 2023-07-11 宝山钢铁股份有限公司 1180MPa级低碳低合金热镀锌TRIP钢及快速热处理热镀锌制造方法

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US20130248055A1 (en) 2013-09-26
EP2439291B1 (fr) 2013-11-27
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